Laser Shock Peening Method for Improving the Corrosion Resistance of Sintered Nd-Fe-B Magnet

ABSTRACT

Disclosed is a surface modification technique for permanent magnetic materials. First, a sintered Nd—Fe—B magnet is immersed in a chlorine-containing solution to corrode its surface after the sintered Nd—Fe—B magnet is ground, polished and cleaned, so that atomic vacancies or gaps are produced at the grain boundaries in the surface layer of the corroded sintered Nd—Fe—B magnet; then, compound nanopowders coated on the surface of the sintered Nd—Fe—B magnet are implanted into the grain boundaries by laser shock peening to obtain a gradient nanostructure layer along the depth direction; at the same time, the surface nanocrystallization of the sintered Nd—Fe—B magnet and a residual compressive stress layer are induced by laser shock peening which remarkably improves the corrosion resistance of the sintered Nd—Fe—B magnet.

I. TECHNICAL FIELD

The present invention relates to the technical field of surface modification of permanent magnetic materials, particularly to a laser shock peening method for improving the corrosion resistance of a sintered Nd—Fe—B magnet.

I. BACKGROUND ART

Nd—Fe—B magnets are permanent magnets having the strongest magnetic force to date. As the third-generation rare earth permanent magnet materials, Nd—Fe—B magnets are widely applied in industries such as energy, transportation, machinery, medical, IT, and household appliances due to their excellent performance. Especially, with the development of the knowledge economy represented by information technology, demand for Nd—Fe—B rare earth permanent magnet industry and other functional materials is increasing, leading to broader market prospects for the Nd—Fe—B industry. However, in humid environments, intergranular corrosion may occur easily in the magnets owing to the existence of Nd-rich phases. Consequently, the corrosion resistance is degraded and the scope of the application of magnets is limited severely. A sintered Nd—Fe—B magnet mainly consists of an Nd—Fe—B principal phase and Nd-rich grain boundary phases, wherein the Nd-rich phases have high activity and low potential, and are easy to be corroded in environments with corrosive media, hot and humid environments, and the like. Since there are high potential differences between the Nd-rich phases and the Nd—Fe—B principal phase, sintered Nd—Fe—B magnets usually exhibit intergranular corrosion behaviors. The low corrosion resistance is a disadvantage of Nd—Fe—B magnets as well as one of the factors limiting their wide application. The corrosion of sintered Nd—Fe—B magnets not only destroys their integrity but also results in compromised magnetic properties, and seriously affects the actual application of magnets. Therefore, since sintered Nd—Fe—B magnets were successfully prepared for the first time in 1983, it has been of great practical significance to study the corrosion mechanism of sintered Nd—Fe—B magnets and improve the corrosion resistance of the magnets based on the corrosion mechanism of the magnets.

At present, the methods for surface protection of sintered Nd—Fe—B magnets mainly include electrogalvanizing, nickel electroplating and electrophoretic coating, etc. However, the surface protection of sintered Nd—Fe—B magnets is still one of the key problems limiting their application up to now due to the weak cohesion and insufficient corrosion resistance of coatings. Obtaining amorphous Ni—P alloys by means of chemical plating is a simple and feasible method, and good corrosion-resistant effects have been achieved as a corrosion-resistant protective coating of many corrosion-prone materials. However, sintered Nd—Fe—B magnet materials have rough and porous surfaces owing to the limitation of the material preparation process. Through numerous experiments, it is found that the traditional chemical plating process still can't fully meet the requirements for protection of magnets. Therefore, it is necessary to develop a new surface modification method for improving the corrosion resistance of sintered Nd—Fe—B magnets.

Laser shock peening (also referred to as laser shock processing) is a new surface strengthening technique. It utilizes the mechanical effect of shock waves induced by high-power laser to process materials, and has characteristics including high pressure, high energy, ultra-fast and ultra-high strain rate and so on. Besides, it causes plastic deformation in the surface layer of the treated material, changing the microstructure of the material in the surface layer, attaining an effect of grain refinement. At the same time, the depth of induced residual stress layer is up to 1˜2 mm. Therefore, the strength, hardness, wear resistance and corrosion resistance properties of the treated material can be remarkably improved.

III. CONTENTS OF THE INVENTION

Based on the corrosion mechanism of sintered Nd—Fe—B magnets, the present invention provides a new surface modification method for improving the corrosion resistance of sintered Nd—Fe—B magnets. Firstly, a sintered Nd—Fe—B magnet is immersed in a chlorine-containing solution to corrode its surface after the Nd—Fe—B magnet is ground, polished and cleaned, so that atomic vacancies or gaps are produced at the grain boundaries in the surface layer of the corroded sintered Nd—Fe—B magnet. Then, compound nanopowders coated on the surface of the sintered Nd—Fe—B magnet are implanted into the grain boundaries by laser shock peening, i.e., under the mechanical effect of the ultra-strong shock wave induced by laser shock peening, the compound nanopowders are implanted into the surface layer of the sintered Nd—Fe—B magnet to obtain a gradient nanostructure layer along the depth direction. The technique can effectively implant compound nanopowders into the surface layer of a sintered Nd—Fe—B magnet under the mechanical effect of ultra-strong shock wave produced by laser shock peening, and thereby modify the compositions and structures of the grain boundary phases so as to improve the physicochemical properties of the grain boundary phases. At the same time, the surface nanocrystallization of the sintered Nd—Fe—B magnet and a compressive residual stress layer are induced by laser shock peening, and the corrosion resistance of the sintered Nd—Fe—B magnet is remarkably improved.

The specific steps are as follows:

-   (1) grinding and polishing the surface of a sintered Nd—Fe—B magnet,     and then immersing the sintered Nd—Fe—B magnet in an alcoholic     solution and removing the dust and oil stains from the surface of     the sintered Nd—Fe—B magnet with an ultrasonic cleaner; -   (2) immersing the sintered Nd—Fe—B magnet into a chlorine-containing     solution to corrode its surface so that atomic vacancies or gaps are     produced at the grain boundaries of the corroded sintered Nd—Fe—B     magnet; -   (3) taking out the pretreated sintered Nd—Fe—B magnet and drying it     by cold air, and then mounting the sintered Nd—Fe—B magnet on a     special fixture controlled by a manipulator; -   (4) setting laser output power and laser spot parameters by means of     a laser control device; specifically, a single-pulse Nd: YAG laser     is used, and the working parameters are as follows: the wavelength     is 1,064 nm, the pulse width is 8-16 ns, the energy per pulse is     5-7.6 J, and radius of the laser spot: 2-3 mm, the overlapping rate     between two neighboring laser spots in both transverse and     longitudinal directions is set to be 50%; at the same time,     superposing the spot center of the laser beam on the top left corner     of the magnet surface to be treated, and taking the position as an     initial position of laser shock peening, and making the X-direction     and Y-direction of the area to be treated in line with the     X-direction and Y-direction of the loading platform; -   (5) uniformly coating compound nanopowders on the corroded surface     of the sintered Nd—Fe—B magnet sample, and turning on the laser at     the same time; controlling the sintered Nd—Fe—B magnet sample with a     manipulator to move to the focus of the laser beam; and carrying out     laser shock peening on the corroded surface of the sintered Nd—Fe—B     magnet; implanting the compound nanopowders into the surface layer     of the sintered Nd—Fe—B magnet sample under the mechanical effect of     the ultra-strong shock wave induced by laser shock peening; at the     same time, inducing a residual compressive stress layer by laser     shock peening so as to obtain a high-performance gradient     nanostructure layer along the depth direction.

In the step (1), the atomic percentage of the sintered Nd—Fe—B magnet is Nd_(a)R_(b)Fe_(100-a-b-c-d)B_(c)M_(d), wherein, 8≤a≤18, 0.5≤b≤5, 3.5≤c≤8, 0.1≤d≤5, R is one or more of Pr, Dy, Tb, Ho, Gd, Ce, Co, Ni, Al, Cu, and Ga elements, and M is one or more of Al, Cu, Ga, Mg, Zn, Sn, Si, Co, Ni, Nb, Zr, Ti, W, and V elements.

In the step (2), the chlorine-containing solution is NaCl solution with a mass fraction of 3.5% or MgCl₂ solution with a mass fraction of 14%, and the immersion time is 30-120 minutes.

In the step (5), the compound nanopowder layer coated in the step (5) is in a thickness of 0.5-1 mm, and the average particle size of the compound nanopowders is 30-150 nm.

In the step (5), the compound nanopowder is AlN nanopowder with a high melting point, which belongs to covalent compounds, has an excellent thermal stability, and can stably exist in grain boundaries.

Technical effects of the present invention: in the present invention, first, a sintered Nd—Fe—B magnet is immersed in a chlorine-containing solution to corrode its surface after the Nd—Fe—B magnet is ground, polished and cleaned, so that atomic vacancies or gaps are produced at the grain boundaries in the surface layer of the corroded sintered Nd—Fe—B magnet. Then, compound nanopowders coated on the surface of the sintered Nd—Fe—B magnet are implanted into the grain boundaries by laser shock peening, i.e., under the mechanical effect of the ultra-strong shock waves produced by laser shock peening, the compound nanopowders are implanted into the surface layer of the sintered Nd—Fe—B magnet to obtain a gradient nanostructure layer along the depth direction, modify the compositions and structures of the grain boundary phases so as to improve the physicochemical properties of the grain boundary phases; at the same time, the surface nanocrystallization of the sintered Nd—Fe—B magnet and a residual compressive stress layer are induced by laser shock peening, and thereby the corrosion resistance of the sintered Nd—Fe—B magnet is improved remarkably.

IV. DESCRIPTION OF DRAWINGS

FIG. 1 shows the surface corrosion morphology of a sintered Nd—Fe—B magnet;

FIG. 2 is a schematic diagram illustrating the comparison between the potentiodynamic polarization curve of a sintered Nd—Fe—B magnet Nd₈Pr₄Fes₈₁Co₂B_(3.5)Cu_(1.5) with AlN nanometer powder and the potentiodynamic polarization curve of a sintered Nd—Fe—B magnet Nd₈Pr₄Fe₈₁Co₂B_(3.5)Cu_(4.5) without AlN nanometer powder in NaCl solution with a mass fraction of 14%;

FIG. 3 is a schematic diagram illustrating the comparison between the potentiodynamic polarization curve of a sintered Nd—Fe—B magnet Nd₁₀Dy₂Fe₇₉B₈Al_(0.5)Mg_(0.5) with AlN nanometer powder and the potentiodynamic polarization curve of a sintered Nd—Fe—B magnet Nd₁₀Dy₂Fe₇₉B₈Al_(0.5)Mg_(0.5) without AlN nanometer powder in NaCl solution with a mass fraction of 3.5%;

FIG. 4 is a schematic diagram illustrating the comparison between the potentiodynamic polarization curve of a sintered Nd—Fe—B magnet Nd₁₅Gd_(0.5)Fe₈₀B₄Ni_(0.5) with AlN nanometer powder and the potentiodynamic polarization curve of a sintered Nd—Fe—B magnet Nd₁₅Gd_(0.5)Fe₈₀B₄Ni_(0.5) without AlN nanometer powder in NaCl solution with a mass fraction of 3.5%.

V. EMBODIMENTS

Hereunder the technical scheme of the present invention will be further detailed in some embodiments with reference to the accompanying drawings.

In the following examples using the above-mentioned strengthening method to process sintered Nd—Fe—B magnets, the steps include:

Embodiment 1

-   (1) The surface of a sintered Nd—Fe—B magnet     Nd₈Pr₄Fe₈₁Co₂B_(3.5)Cu_(1.5) is ground and polished with 500 #-2400     #SiC abrasive paper, and then the sintered Nd—Fe—B magnet is     immersed in an alcoholic solution to remove the dust and oil stains     from the surface of the sintered Nd—Fe—B magnet with an ultrasonic     cleaner; -   (2) The sintered Nd—Fe—B magnet is immersed into NaCl solution with     a mass fraction of 14% and held for 30 minutes so that atomic     vacancies or gaps are produced at the grain boundaries when the     surface of the sintered Nd—Fe—B magnet is corroded; -   (3) The pretreated sintered Nd—Fe—B magnet is taken out and dried by     cold air, and then the sintered Nd—Fe—B magnet is mounted on a     special fixture controlled by a manipulator; -   (4) The laser output power and laser spot parameters are set by     means of a laser control device; specifically, a single-pulse Nd:YAG     laser is used, and the working parameters are as follows: the     wavelength is 1,064 nm, the pulse width is 16 ns, the energy per     pulse is 5.6 J, the radius of the laser spot is 3 mm, and the     overlapping rate between two neighboring laser spots in both     transverse and longitudinal directions is set to be 50%; at the same     time, the spot center of the laser beam is superposed on the top     left corner of the magnet surface to be treated and the position is     taken as an initial position of laser shock peening, and the     X-direction and Y-direction of the area to be treated is kept in     line with the X-direction and Y-direction of the loading platform; -   (5) AlN compound nanopowders with an average particle size of 50 nm     are uniformly coated on the surface of the sintered Nd—Fe—B magnet     sample, wherein, the thickness of the coating is 0.5 mm; after     turning on the laser, the sintered Nd—Fe—B magnet sample is     controlled with a manipulator to move to the focus of the laser     beam, and massive laser shock peening is carried out on the surface     of the magnet using a line-by-line processing method; the AlN     compound nanopowders are implanted into the surface layer of the     sintered Nd—Fe—B magnet under the mechanical effect of the     ultra-strong shock wave produced by laser shock peening, and a     residual compressive stress layer is induced by laser shock peening     at the same time so as to obtain a high-performance gradient     nanostructure layer along the depth direction.     -   In this embodiment, an electrochemical corrosion test is carried         out for the sintered Nd—Fe—B magnet         Nd₈Tb₃Fe₈₃Co₂B_(3.5)Cu_(1.5), and the test result is compared         with that of the sintered Nd—Fe—B magnet before treatment. It is         seen from FIG. 2: after adding the AlN compound nanopowders, the         corrosion potential of the sample increases, and the corrosion         current density decreases. The test result indicates: adding AlN         nanometer powders at the grain boundaries decreases the quantity         of Nd-rich phases in the grain boundary area, the corrosion         potential of the grain boundary phases increases, and the         stability of the grain boundaries is improved. According to the         mechanism of electrode reaction, the increase of potential of         the grain boundary phases leads to the increase of corrosion         potential of the entire sintered Nd—Fe—B magnet. The result         further demonstrates that adding AlN nanometer powder at the         grain boundaries can remarkably improve the corrosion resistance         of the sintered Nd—Fe—B magnet Nd₈Pr₄Fe₈₃Co₂B_(3.5)Cu_(1.5).

Embodiment 2

-   (1) The surface of a sintered Nd—Fe—B magnet     Nd₁₀Dy₂Fe₇₉B₈Al_(0.5)Mg_(0.5) is ground and polished with 500 #-2400     #SiC abrasive paper, and then the sintered Nd—Fe—B magnet is     immersed in an alcoholic solution to remove the dust and oil stains     from the surface of the sintered Nd—Fe—B magnet with an ultrasonic     cleaner; -   (2) The sintered Nd—Fe—B magnet is immersed into NaCl solution with     a mass fraction of 3.5% and held for 60 minutes so that atomic     vacancies or gaps are produced at the grain boundaries when the     surface of the sintered Nd—Fe—B magnet is corroded; -   (3) The pretreated sintered Nd—Fe—B magnet is taken out and dried by     cold air, and then the sintered Nd—Fe—B magnet is mounted on a     special fixture controlled by a manipulator, -   (4) The laser output power and laser spot parameters are set by     means of a laser control device; specifically, a single-pulse Nd:YAG     laser is used, and the working parameters are as follows: the     wavelength is 1,064 nm, the pulse width is 8 ns, the energy per     pulse is 7.6 J, the radius of the light spot is 3 mm, and the     overlapping rate between two neighboring laser spots in both     transverse and longitudinal directions is set to be 50%; at the same     time, the spot center of the laser beam is superposed on the top     left corner of the magnet surface to be treated and the position is     taken as an initial position of laser shock peening, and the     X-direction and Y-direction of the area to be treated is kept in     line with the X-direction and Y-direction of the loading platform; -   (5) AlN compound nanopowders with an average particle size of 150 nm     are uniformly coated on the surface of the sintered Nd—Fe—B magnet     sample, wherein, the thickness of the coating is 1 mm; after turning     on the laser, the sintered Nd—Fe—B magnet sample is controlled with     a manipulator to move to the focus of the laser beam, and massive     laser shock peening is carried out on the surface of the magnet     using a line-by-line processing method; the AlN compound nanopowders     are implanted into the surface layer of the sintered Nd—Fe—B magnet     under the mechanical effect of the ultra-strong shock wave produced     by laser shock peening, and a residual compressive stress layer is     induced by laser shock peening at the same time so as to obtain a     high-performance gradient nanostructure layer along the depth     direction.     -   In this embodiment, an electrochemical corrosion test is carried         out for the sintered Nd—Fe—B magnet         Nd₈Pr₄Fe₈₃Co₂B_(3.5)Cu_(1.5), and the test result is compared         with that of the sintered Nd—Fe—B magnet before treatment.         Likewise, it is seen from FIG. 3: after adding the AlN compound         nanopowders, the corrosion potential of the sample increases,         and the corrosion current density decreases.

Embodiment 3

-   (1) The surface of a sintered Nd—Fe—B magnet     Nd₁₅Gd_(0.5)Fe₈₀B₄Ni_(0.5) is ground and polished with 500 #-2400     #SiC abrasive paper, and then the sintered Nd—Fe—B magnet is     immersed in an alcoholic solution to remove the dust and oil stains     from the surface of the sintered Nd—Fe—B magnet with an ultrasonic     cleaner; -   (2) The sintered Nd—Fe—B magnet is immersed into NaCl solution with     a mass fraction of 3.5% and held for 90 minutes so that atomic     vacancies or gaps are produced at the grain boundaries when the     surface of the sintered Nd—Fe—B magnet is corroded; -   (3) The pretreated sintered Nd—Fe—B magnet is taken out and dried by     cold air, and then the sintered Nd—Fe—B magnet is mounted on a     special fixture controlled by a manipulator; -   (4) The laser output power and laser spot parameters are set by     means of a laser control device; specifically, a single-pulse Nd:YAG     laser is used, and the working parameters are as follows: the     wavelength is 1,064 un, the pulse width is 10 ns, the energy per     pulse is 6 J, the radius of the laser spot is 3 mm, and the     overlapping rate between two neighboring laser spots in both     transverse and longitudinal directions is set to be 50%; at the same     time, the spot center of the laser beam is superposed on the top     left corner of the magnet surface to be treated and the position is     taken as an initial position of laser shock peening, and the     X-direction and Y-direction of the area to be treated is kept in     line with the X-direction and Y-direction of the loading platform; -   (5) AlN compound nanopowders with an average particle size of 100 nm     are uniformly coated on the surface of the sintered Nd—Fe—B magnet     sample, wherein, the thickness of the coating is 0.7 mm; after     turning on the laser, the sintered Nd—Fe—B magnet sample is     controlled with a manipulator to move to the focus of the laser     beam, and massive laser shock peening is carried out on the surface     of the magnet using a line-by-line processing method, the AlN     compound nanopowders are implanted into the surface layer of the     sintered Nd—Fe—B magnet under the mechanical effect of the super     strong shock wave produced by laser shock peening, and a residual     compressive stress layer is induced by laser shock peening at the     same time so as to obtain a high-performance gradient nanostructure     layer along the depth direction.     -   In this embodiment, an electrochemical corrosion test is carried         out for the sintered Nd—Fe—B magnet         Nd₈Pr₄Fe₈₃Co₂B_(3.5)Cu_(1.5), and the test result is compared         with that of the sintered Nd—Fe—B magnet before treatment.         Likewise, it is seen from FIG. 4: after adding the AlN compound         nanopowders, the corrosion potential of the sample increases,         and the corrosion current density decreases. 

1: A laser shock peening method for improving the corrosion resistance of a sintered Nd—Fe—B magnet, wherein: first, a sintered Nd—Fe—B magnet is immersed in a chlorine-containing solution to corrode its surface slightly after the sintered Nd—Fe—B magnet is ground, polished and cleaned, so that atomic vacancies or gaps are produced at the original grain boundaries of the corroded sintered Nd—Fe—B magnet; then, compound nanopowders coated on the surface of the sintered Nd—Fe—B magnet are implanted into the grain boundaries by laser shock peening, to form a gradient nanostructure layer along the depth direction; at the same time, the surface nanocrystallization of the sintered Nd—Fe—B magnet and a residual compressive stress layer are induced by laser shock peening; whereupon the compositions and structures of the grain boundary phases are modified, and the physicochemical properties of the grain boundary phases are improved, an effect of inhibiting grain boundary corrosion in the surface of the magnet is achieved, and corrosion resistance of the sintered Nd—Fe—B magnet is improved remarkably, wherein, the chlorine-containing solution is NaCl solution with a mass fraction of 3.5% or MgCl₂ solution with a mass fraction of 14%, and the immersion time is 30-120 minutes; the compound nanopowder is AlN nanometer powder with a high melting point, which belongs to covalent compounds, has an excellent thermal stability, and can stably exist in grain boundaries; the atomic percentage of the sintered Nd—Fe—B magnet is Nd_(a)R_(b)Fe_(100-a-b-c-d)B_(c)M_(d), wherein, 8≤a≤18, 0.5≤b≤5, 3.5≤c≤8, 0.1≤d≤5, R is one or more of Pr, Dy, Tb, Ho, Gd, Ce, Co, Ni, Al, Cu, and Ga elements, and M is one or more of Al, Cu, Ga, Mg, Zn, Sn, Si, Co, Ni, Nb, Zr, Ti, W, and V elements; the laser is a single-pulse Nd:YAG laser, and the working parameters are as follows: the wavelength is 1,064 nm, the pulse width is 8-16 ns, the energy per pulse is 5-7.6 J, and the laser spot radius is 2-3 mm. 2: The laser shock peening method for improving the corrosion resistance of a sintered Nd—Fe—B magnet according to claim 1 comprising the steps of: (1) grinding and polishing the surface of a sintered Nd—Fe—B magnet, and then immersing the sintered Nd—Fe—B magnet in an alcoholic solution and removing the dust and oil stains from the surface of the sintered Nd—Fe—B magnet with an ultrasonic cleaner; (2) immersing the sintered Nd—Fe—B magnet into a chlorine-containing solution to corrode its surface so that atomic vacancies or gaps are produced at the grain boundaries of the corroded sintered Nd—Fe—B magnet; (3) removing the pretreated sintered Nd—Fe—B magnet from the chlorine-containing solution and drying it in air, and then mounting the sintered Nd—Fe—B magnet on a fixture controlled by a manipulator; (4) setting laser output power and laser spot parameters by a laser control device; at the same time, superposing the spot center of the laser beam on the top left corner of the magnet surface to be treated and taking the position as an initial position of laser shock peening, and making the X-direction and Y-direction of the area to be treated in line with the X-direction and Y-direction of the loading platform; (5) uniformly coating compound nanopowders on the surface of the sintered Nd—Fe—B magnet sample, and turning on the laser at the same time; controlling the sintered Nd—Fe—B magnet sample with a manipulator to move to the focus of the laser beam, and carrying out laser shock peening on the corroded surface of the sintered Nd—Fe—B magnet using a line-by-line processing method; implanting the compound nanopowders into the surface layer of the sintered Nd—Fe—B magnet sample under the mechanical effect of the ultra-strong shock wave produced by laser shock peening; and inducing a residual compressive stress layer by laser shock peening so as to obtain a high-performance gradient nanostructure layer along the depth direction. 3: The laser shock peening method for improving the corrosion resistance of a sintered Nd—Fe—B magnet according to claim 2, wherein, in step (4), the overlapping rate between two neighboring laser spots in both transverse and longitudinal directions is set to be 50%. 4: The laser shock peening method for improving the corrosion resistance of a sintered Nd—Fe—B magnet according to claim 2, wherein, in the step (5), the thickness of the compound nanopowder layer coated in step (5) is 0.5-1 mm, and the average particle size of the compound nanopowders is 30-150 nm. 